EP1642991B1 - Verfahren zum warmumformen und warmumgeformtes element - Google Patents

Verfahren zum warmumformen und warmumgeformtes element Download PDF

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EP1642991B1
EP1642991B1 EP04735124A EP04735124A EP1642991B1 EP 1642991 B1 EP1642991 B1 EP 1642991B1 EP 04735124 A EP04735124 A EP 04735124A EP 04735124 A EP04735124 A EP 04735124A EP 1642991 B1 EP1642991 B1 EP 1642991B1
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Prior art keywords
forming
hot
hardness
steel sheet
cooling rate
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English (en)
French (fr)
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EP1642991A4 (de
EP1642991A1 (de
Inventor
Toshinobu Sumitomo Metal Indust. Ltd NISHIBATA
Masahiro Sumitomo Metal Indust. Ltd NAKATA
Shuntaro Toyota Jidosha Kabushiki Kaisha SUDO
Akira Toyoda Iron Works Co. Ltd. OBAYASHI
Masanobu Toyoda Iron Works Co. Ltd. ICHIKAWA
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Nippon Steel Corp
Toyoda Iron Works Co Ltd
Toyota Motor Corp
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Toyoda Iron Works Co Ltd
Sumitomo Metal Industries Ltd
Toyota Motor Corp
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working

Definitions

  • This invention relates to a hot formed member such as a mechanical structural part including a structural part of an automobile body and an automobile suspension part, and to a hot forming method used for its manufacture. More specifically, the present invention relates to a hot press-formed member and a hot press forming method for its manufacture.
  • hot press forming as an example, but the present invention can also be applied to different types of hot forming other than press forming, such as roll forming and forging.
  • die cooling in a hot press forming method has the problems that the quenching hardness of the resulting formed member is inadequate and remains at the level of Hv 400 - 490 in the case of a 0.2% C steel material, and that the hardness of the formed member extremely varies locally.
  • JP 08-269615 A1 discloses a hot rolled steel sheet for rapid quenching which comprises C: 0.18 - 0.30%, Si: 0.01 - 1.0%, Mn: 0.2 - 1.5%, P: at most 0.03%, S: at most 0.02%, sol. Al: at most 0.08%, Cr: 0.1 - 0.5%, B: 0.0006 - 0.0040%, N: at most 0.01%, optionally at least one of Cu: at most 0.5%, Ni: at most 0.3%, and Ti: 0.01 - 0.05%, and a remainder of iron.
  • This steel sheet is given a high strength by high frequency hardening after it is cold worked.
  • EP-A1-1,143,029 discloses a method in accordance with the precharacterizing section of claim 1.
  • WO 03/035922 discloses a method of hot rolling steel sheet and subsequent galvanising.
  • the present invention provides a hot formed member which can be manufactured from a high strength steel sheet by hot forming and which has a stabilized strength and toughness, and it also provides a hot forming method for its manufacture.
  • the present invention provides a hot press-formed member such as a mechanical structural part including a structural part of an automobile body and an automobile suspension part and a hot press forming method used for its manufacture.
  • the present invention provides a hot forming method comprising heating a steel sheet having a steel composition consisting of, in mass percent, C: 0.15 - 0.45%; Mn: 0.5 - 3.0%; Cr: 0.1 - 0.5%; Ti: 0.01 - 0.1%; B: 0.0002 - 0.004%; Si: at most 0.5%, P: at most 0.05%; S: at most 0.05%, Al: at most 1%, N: at most 0.01 %; one or more of Ni: at most 2%, Cu: at most 1%, Mo: at most 1%, V: at most 1%, and Nb: at most 1%; and a remainder of Fe and unavoidable impurities to a temperature of the Ac 3 point or higher, holding it at that temperature, and then forming the heated steel sheet to the shape of a finished member, wherein the formed member is quenched by cooling from the forming temperature during forming or after forming in such a manner that the cooling rate to the Ms point is at least the critical cooling rate and characterized
  • the present invention provides a hot formed member made from a steel sheet having a steel composition consisting of, in mass percent, C: 0.15 - 0.45%; Mn: 0.5 - 3.0%; Cr: 0.1 - 0.5%; Ti: 0.01 - 0.1%; B: 0.0002 - 0.004%; Si: at most 0.5%; P: at most 0.05%; S: at most 0.05%; Al: at most 1 %; N: at most 0.01 %; one or more of Ni: at most 2%, Cu: at most 1 %, Mo: at most 1 %, V: at most 1 %, and Nb: at most 1 %; and a remainder of Fe and unavoidable impurities, characterized in that the hardness after hot forming expressed in Vickers hardness is less than the value of (maximum quenching hardness - 10) and at least the value of (maximum quenching hardness - 100) and in that the member has an auto-tempered martensite structure, wherein the maximum quenching hard
  • a hot formed member with a stabilized strength and toughness can be manufactured by hot forming in which during cooling after forming, such as during die cooling, the average cooling rate in a temperature region extending downwards from the Ms point (the temperature at which martensite begins to form from austenite) is restricted within certain limits.
  • the present invention relates to a hot forming method in which a steel sheet having a steel composition consisting essentially, in mass percent, of C: 0.15 - 0.45%, Mn: 0.5 - 3.0%, Cr: 0.1 - 0.5%, Ti: 0.01 - 0.1 %, B: 0.0002 - 0.004%, Si: at most 0.5%, P: at most 0.05%, S: at most 0.05%, Al: at most 1%, N: at most 0.01 %, one or more of Ni: at most 2%, Cu: at most 1%, Mo: at most 1%, V: at most 1%, and Nb: at most 1%, and a remainder of Fe and unavoidable impurities is heated to a temperature of at least the Ac 3 point of the steel and held at that temperature before it is formed into the shape of a finished member.
  • quenching is carried out by cooling in such a manner that the cooling rate of the resulting formed member to the Ms point (until the Ms point is reached) is at least the critical cooling rate, and such that the average cooling rate from the Ms point to 200°C is in the range of 25 - 150°C/s.
  • the critical cooling rate means the upper critical cooling rate.
  • the present invention relates to a hot formed member made from a steel sheet having the above-described steel composition.
  • the hot formed member has a hardness on the Vickers scale after hot forming, the hardness being less than the value of (maximum quenching hardness - 10) and not less than the value of (maximum quenching hardness - 100).
  • the hot forming is hot press forming which is carried out using a pair of press forming dies.
  • the present invention greatly contributes to a broadening of the uses for press formed members of high strength steel sheets.
  • percent with respect to the steel composition i.e., the chemical composition of the steel means mass percent.
  • Carbon (C) is an extremely important element because it increases the hardenability of a steel sheet and it primarily determines the strength thereof after hardening. In addition, it is an element which lowers the Ac 3 point of a steel and promotes a decrease of the heating temperature required for hardening (quenching). If the C content is less than 0.15%, these effects cannot be achieved adequately, while if the C content exceeds 0.45%, there is a marked decrease in the toughness of hardened portions.
  • the lower limit of the C content is 0.16% and the upper limit thereof is 0.35%.
  • Manganese (Mn) is an element which is extremely effective for increasing the hardenability of a steel sheet and stably guaranteeing strength after hardening. In addition, it is an element which lowers the Ac 3 point and promotes a decrease in the heating temperature required for hardening. If the Mn content is less than 0.5%, these effects cannot be attained adequately, while an Mn content exceeding 3.0% results in the effects thereof saturating and leads to a decrease in the toughness of hardened portions. A preferred Mn content is 0.8 - 2.0%.
  • Chromium is an element which is effective for increasing the hardenability of a steel sheet and stably guaranteeing strength after hardening. If the Cr content is less than 0.1 %, these effects cannot be attained adequately, while if the Cr content exceeds 0.5%, its effects saturate, leading to a needless increase in costs. A preferred Cr content is 0.15 - 0.30%.
  • Titanium (Ti) is an element which is effective for increasing the hardenability of a steel sheet and stably guaranteeing strength after hardening. In addition, it has the effect of increasing the toughness of hardened portions. If the Ti content is less than 0.01 %, these effects are not adequate, while if the Ti content exceeds 0.1 %, its effects saturate, leading to a needless increase in cost. A preferred Ti content is 0.015 - 0.03%.
  • B Boron
  • Si at most 0.5%
  • P at most 0,05%
  • S 0.05%
  • Al at most 1%
  • N at most 0.01%
  • Each of these elements also has the effects of increasing the hardenability of a steel sheet and increasing the stability of the strength after hardening. However, if the respective contents exceed the above-described respective upper limits, the effects thereof saturate and lead to an increase in costs.
  • Ni at most 2%
  • Cu at most 1%
  • Mo at most 1%
  • V at most 1%
  • Nb at most 1%
  • a steel sheet used in the present invention is heated to a temperature in the austenite region during heating prior to forming, thereby causing austenitic transformation. Therefore, the mechanical properties at room temperature prior to heating are not critical, and there are no particular restrictions on the metallic structure prior to heating. Accordingly, the steel sheet to be worked may be a hot rolled steel sheet, a cold rolled steel sheet, or a plated steel sheet, and there are no particular restrictions on its method of manufacture.
  • Examples of plated steel sheets are aluminum-based plated steel sheets (namely, steel sheets with an aluminum plating or an aluminum alloy plating) and zinc-based steel sheets (namely, steel sheets with a zinc plating or a zinc alloy plating).
  • a plated steel sheet may be either an electroplated steel sheet or a hot dip plated steel sheet.
  • a galvannealed steel sheet may also be used.
  • the steel sheet In die cooling at the time of hot press forming, in order to achieve hardening of a formed member, i.e., of a hot press-formed member after forming, it is necessary to initially heat the steel sheet to be worked to a temperature in the austenite region in order to allow the steel sheet to have the structure of an austenite phase.
  • the steel sheet is heated to a temperature of at least the Ac 3 point and held at that temperature for a certain period, which is at least 1 minute under usual conditions.
  • the upper limit on the holding time is preferably on the order of 10 minutes.
  • the cooling rate of a hot press-formed member during hot press forming is a parameter which performs an extremely important role in obtaining stabilized strength and toughness in the member.
  • the structure after hot press forming be not a completely martensitic structure but that it be the structure of auto-tempered martensite.
  • cooling in the range down to the Ms point is performed at a cooling rate equal to or higher than the critical cooling rate so that diffusional transformation does not take place, and in the subsequent temperature range from the Ms point to 200 °C, slow cooling is carried out at an average cooling rate of 25 - 150 °C/s.
  • the average cooling rate from the Ms point to 200 °C is preferably in the range of 30 - 120 °C/s.
  • the types of forming by a hot press forming method include bending, drawing, bulging, bore expanding, and flange forming.
  • the present invention can also be applied to forming methods other than press forming, such as roll forming, as long as a means is provided for cooling a steel sheet during forming or immediately thereafter.
  • a member manufactured by the above-described hot press forming method is a member having an auto-tempered martensitic structure which has minimized variations in strength and excellent toughness.
  • the strength which is obtained is that typical of an auto-tempered martensitic structure, so expressing it as a hardness (Hv), it is lower than the value of (maximum quenching hardness - 10) or ("maximum quenching hardness" minus "10").
  • Hv hardness
  • the hardness is at least the value of (maximum quenching hardness - 100) or ("maximum quenching hardness" minus "100").
  • Hv exceeds the value of (maximum quenching hardness - 10)
  • the member has a decreased toughness, while if it is lower than the value of (maximum quenching hardness - 100), the member has a decreased strength.
  • a preferred value of Hv is at most the value of (maximum quenching hardness - 20) and at least the value of (maximum quenching hardness - 80).
  • the “maximum quenching hardness” used herein is the hardness obtained when a material is held for 10 minutes in a salt bath heated to 900 °C and is then water cooled.
  • a pair of steel dies for use in hot press forming a steel sheet are maintained at room temperature or at a temperature of several tens of degrees C, so at the time of hot press forming, a press formed member is cooled by means of the steel dies.
  • the dimensions of the dies may be changed to vary their heat capacity.
  • the cooling rate can also be varied by changing the material of the dies to a different metal (such as copper).
  • the cooling rate can be varied by using water-cooled dies and changing the flow rate of cooling water used to cool the dies.
  • the cooling rate of a press formed member can be varied by, for example, using dies having grooves which are previously cut therein in a plurality of locations and passing water through the grooves while the dies are in a press, or by raising a die in the course of press forming and passing water between the die and the press-formed member.
  • steel sheets having the compositions shown in Table 1 were used as steel sheets to be worked. These steel sheets were manufactured from slabs, which were prepared by melting in a laboratory, by hot rolling and subsequent cold rolling. For Steel No. 2, hot dip galvanizing (with a zinc coating weight of 60 g/m 2 per side) was applied using a plating simulator, and then alloying heat-treatment (galvannealing) (to an Fe content in the plating film of 15 mass %) was carried out.
  • each steel material was held for 10 minutes in a salt bath heated to 900 °C and then subjected to water cooling. The hardness obtained by quenching in this manner was taken as the maximum quenching hardness.
  • a cylindrical test piece ( Figure 2 ) having a diameter of 3.0 mm and a length of 10 mm was cut from a hot rolled steel sheet.
  • the test piece was heated in air to 950 °C at a rate of temperature increase of 10 °C/s and held for 5 minutes at that temperature, and then it was cooled to room temperature at various cooling rates.
  • the Ac 3 point and the Ms point were determined.
  • measurement of the Vickers hardness (with a load of 49 N, 5 measurements) of the resulting test piece and observation of the structure were carried out, and from these results, the critical cooling rate was estimated.
  • Runs Nos. 1-4 which are examples of the this invention, the average cooling rate from the Ms point to 200 °C was suitable, so the resulting hardness was lower than the value of (maximum quenching hardness - 10) and higher than the value of (maximum quenching hardness - 100).
  • Run No. 5 which was a comparative example, cooling was performed at greater than the critical cooling rate, but the average cooling rate from the Ms point to 200 °C was too slow, so sufficient hardness was not obtained.
  • Run No. 6 which was also a comparative example, the average cooling rate from the Ms point to 200 °C was too fast, so the hardness became too high.
  • the meaning of "too high" for hardness is not that the absolute value of the hardness was too high but that it was close to the maximum quenching hardness.
  • Figure 1 is a schematic diagram illustrating the hat-shaped press forming method used herein using a pair of dies in the form of a die and a punch.
  • the hot press forming conditions which were used were a forming height of 70 mm, Rd (R of the die shoulder portion) of 8 mm, Rp (R of the punch shoulder portion) of 8 mm, a clearance of 1.0 mm, and a blank holder pressure of 12.7 kN.
  • the Vickers hardness of the resulting hot press-formed article was measured in various portions thereof including the punch bottom portion, a central portion of the side wall, and the flange portion (with a load of 9.8 N, 5 measurements). In addition, the rate of cooling in each of these portions during cooling was measured by a thermocouple which was adhered to each portion. The results are compiled in Table 3. Table 3 Average cooling rate from the Ms point to 200°C (°C/s) Hardness after hot press forming (Hv) Punch bottom portion 55 460 Center of side wall 100 471 Flange portion 120 480

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Claims (5)

  1. Warmverformungsverfahren, welches umfasst: Erhitzen eines Stahlblechs mit einer Stahlzusammensetzung bestehend aus in Masseprozent C: 0,15 - 0,45%; Mn: 0,5 - 3,0%; Cr: 0,1 - 0,5%; Ti: 0,01 - 0,1 %; B: 0,0002 -0,004%; Si: höchstens 0,5%; P: höchstens 0,05%; S: höchstens 0,05%; Al: höchstens 1 %; N: höchstens 0,01 %; einem oder mehreren von: Ni: höchstens 2%, Cu: höchstens 1 %; Mo: höchstens 1 %; V: höchstens 1 % und Nb: höchstens 1%; und einem Rest aus Fe und unvermeidbaren Verunreinigungen auf eine Temperatur des Ac3-Punkts oder höher, Halten desselben bei dieser Temperatur und dann Verformen des erhitzten Stahlblechs zu der Form eines fertigen Elements, wobei das geformte Element durch Abkühlen von der Verformungstemperatur während oder nach der Verformung so abgeschreckt wird, dass die Abkühlgeschwindigkeit auf den Ms-Punkt mindestens die kritische Abkühlgeschwindigkeit ist, und dadurch gekennzeichnet, dass die durchschnittliche Abkühlgeschwindigkeit des geformten Elements vom Ms-Punkt auf 200°C in dem Bereich von 25 - 150°C/s liegt, um dadurch eine selbstgehärtete Martensitstruktur zu erhalten.
  2. Warmverformungsverfahren nach Anspruch 1, dadurch gekennzeichnet, dass die Verformung unter Verwenden eines Paars von Pressformwerkzeugen ausgeführt wird.
  3. Warmverformungsverfahren nach Anspruch 1 oder Anspruch 2, dadurch gekennzeichnet, dass die Verformung unter Verwenden eines Paars von Pressformwerkzeugen ausgeführt wird und nach dem Verformen das Abkühlen durch Einspritzen von Wasser zwischen die Werkzeuge ausgeführt wird.
  4. Warmverformtes Element, das aus einem Stahlblech mit einer Stahlzusammensetzung bestehend aus in Masseprozent: C: 0,15 - 0,45%; Mn: 0,5 - 3,0%; Cr: 0,1 -0,5%; Ti: 0,01 - 0,1%; B: 0,0002 - 0,004%; Si: höchstens 0,5%; P: höchstens 0,05%; S: höchstens 0,05%; Al: höchstens 1%; N: höchstens 0,01 %; einem oder mehreren von: Ni: höchstens 2%; Cu: höchstens 1%, Mo: höchstens 1%; V: höchstens 1% und Nb: höchstens 1 %; und einem Rest aus Fe und unvermeidbaren Verunreinigungen besteht, dadurch gekennzeichnet, dass die Härte ausgedrückt in Vickers-Härte nach dem Verformen kleiner als der Wert von (maximale Abschreckungshärte - 10) und mindestens der Wert von (maximale Abschreckungshärte - 100) ist und dass das Element eine selbstgehärtete Martensitstruktur aufweist, wobei die maximale Abschreckungshärte die Härte ist, die erhalten wird, wenn ein Material 10 Minuten lang in einem auf 900°C erhitzten Salzbad gehalten wird und dann mit Wasser abgekühlt wird.
  5. Warmverformtes Element nach Anspruch 4, dadurch gekennzeichnet, dass das Warmverformen ein Warmpressverformen ist.
EP04735124A 2003-05-28 2004-05-27 Verfahren zum warmumformen und warmumgeformtes element Expired - Lifetime EP1642991B1 (de)

Applications Claiming Priority (2)

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JP2003151106A JP4325277B2 (ja) 2003-05-28 2003-05-28 熱間成形法と熱間成形部材
PCT/JP2004/007654 WO2004106573A1 (ja) 2003-05-28 2004-05-27 熱間成形法と熱間成形部材

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EP1642991A1 EP1642991A1 (de) 2006-04-05
EP1642991A4 EP1642991A4 (de) 2006-09-27
EP1642991B1 true EP1642991B1 (de) 2009-02-18

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US (1) US7559998B2 (de)
EP (1) EP1642991B1 (de)
JP (1) JP4325277B2 (de)
KR (1) KR100707239B1 (de)
CN (1) CN100453676C (de)
DE (1) DE602004019531D1 (de)
WO (1) WO2004106573A1 (de)

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WO2011121118A2 (de) 2010-04-01 2011-10-06 Thyssenkrupp Steel Europe Ag Stahl, stahlflachprodukt, stahlbauteil und verfahren zur herstellung eines stahlbauteils
DE102010056265B3 (de) * 2010-12-24 2012-05-03 Voestalpine Stahl Gmbh Verfahren zum Erzeugen gehärteter Bauteile
WO2012085253A2 (de) 2010-12-24 2012-06-28 Voestalpine Stahl Gmbh Verfahren zum erzeugen gehärteter bauteile mit bereichen unterschiedlicher härte und/oder duktilität
DE102010056264A1 (de) 2010-12-24 2012-06-28 Voestalpine Stahl Gmbh Verfahren zum Erzeugen gehärteter Bauteile
DE102011053941A1 (de) 2011-09-26 2013-03-28 Voestalpine Stahl Gmbh Verfahren zum Erzeugen gehärteter Bauteile mit Bereichen unterschiedlicher Härte und/oder Duktilität
DE102011053939A1 (de) 2011-09-26 2013-03-28 Voestalpine Stahl Gmbh Verfahren zum Erzeugen gehärteter Bauteile
DE102013100682B3 (de) * 2013-01-23 2014-06-05 Voestalpine Metal Forming Gmbh Verfahren zum Erzeugen gehärteter Bauteile und ein Strukturbauteil, welches nach dem Verfahren hergestellt ist
WO2015120205A1 (en) * 2014-02-05 2015-08-13 Arcelormittal S.A. Hot formable, air hardenable, weldable, steel sheet
WO2016192993A1 (de) 2015-05-29 2016-12-08 Voestalpine Stahl Gmbh Verfahren zum kontaktlosen kühlen von stahlblechen und vorrichtung hierfür
DE102015113056A1 (de) 2015-08-07 2017-02-09 Voestalpine Metal Forming Gmbh Verfahren zum kontaktlosen Kühlen von Stahlblechen und Vorrichtung hierfür

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JP4513608B2 (ja) * 2004-10-29 2010-07-28 住友金属工業株式会社 熱間プレス鋼板部材、その製造方法
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US20060185774A1 (en) 2006-08-24
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CN100453676C (zh) 2009-01-21
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